Method for preparing glass-ceramics, capable of adjusting machinability or translucency through change in temperature of heat treatment

ABSTRACT

Provided is a method for preparing a lithium disilicate glass-ceramics containing silicate as a main component, and more particularly, to a method for preparing a glass-ceramics, which is capable of adjusting machinability or translucency according to a crystalline size by using a first heat treatment or a second heat treatment. To this end, a method for preparing a glass-ceramics containing a silica crystalline phase includes: performing a first heat treatment on a glass composition at a temperature of 400 to 850° C., so that a lithium disilicate crystalline phase and a silica crystalline phase each having a size of 5 to 2,000 nm are formed through the first heat treatment. After the first heat treatment, the method further includes performing a second heat treatment at a temperature of 780 to 880° C., so that translucency is adjusted by a temperature of the second heat treatment.

BACKGROUND OF THE INVENTION Field of the Invention

The present invention relates to a method for preparing a lithiumdisilicate glass-ceramics containing silicate as a main component, andmore particularly, to a method for preparing a glass-ceramics, which iscapable of adjusting a crystalline size, translucency, and machinabilityby using a first heat treatment or a second heat treatment.

Description of the Related Art

With economic development and increased income, an interest inappearance has been increased, and an interest in aesthetics of dentalprosthetic materials has been increased in response to the interest inappearance. As a result, various kinds of dental prosthetic restorationmaterials with the aesthetics are introduced, and among them, variousnon-metal crown materials without using metals have been developed.

The crown materials mean prosthetic materials for restoring enamel anddentin parts of the damaged tooth. The crown materials are classifiedinto inlay, onlay, veneer, crown, and the like according to an appliedregion. Since the region restored by the crown material is the outersurface of the tooth, the aesthetics is highly required and the highstrength is required due to fractures such as abrasion and chipping ofantagonist teeth. Materials which are used as the crown materials in therelated art are leucite glass-ceramics, reinforced porcelain, orfluorapatite (Ca₅(PO₄)₃F) glass-ceramics. Even thought the materialshave the excellent aesthetics, there is a disadvantage in that thepossibility of fracture is high due to low strength of 80 to 120 MPa.Therefore, currently, studies of developing various high-strength crownmaterials have been conducted.

Lithium silicate glass-ceramics was introduced by Marcus P. Borom andAnna M. Turkalo (The Pacific Coast Regional Meeting, The AmericanCeramic Society, San Francisco, Calif., Oct. 31, 1973 (Glass division,No. 3-G-73P)) in 1973. The formation of various crystalline nuclei andthe crystalline and the strength for each growth heat treatmentcondition were studies by using Li₂O—Al₂O₃—SiO₂—Li₂O—K₂O—B₂O₃—P₂O₅-basedglasses. When the high-temperature lithium disilicate crystalline isshown from low-temperature lithium metasilicate, the strength of 30 to35 Kpsc (kilogram per square centimeter: Kg/cm²) is shown. The strengthis caused by residual stress due to a difference in thermal expansioncoefficient between base glass, mother glass, Li₂SiO₅, and Li₂SiO₃crystals.

A material and a method for manufacturing an artificial tooth(monolithic dental crown) by using glass containing a lithium disilicatecrystal are disclosed in a plurality of patent documents. However,according to the known techniques, due to a coarse crystalline phase, itis difficult to directly machine the glass containing the lithiumdisilicate crystal. In order for machining, it is necessary to primarilyform and machine a lithium metasilicate crystalline phase (machinablecrystalline) and secondarily form a high-strength lithium disilicatecrystalline phase by performing a heat treatment. Thus, dimensionaccuracy is lowered due to shrinkage caused by the heat treatment, andit is inconvenient to additionally perform the heat treatment.Generally, since CAD/CAM machining is directly performed in a dentalclinic and needs to be applied to a patient as quickly as possible(one-day appointment), a time delay due to a heat treatment imposesfinancial difficulties on a patient and a user.

In addition, since an existing lithium disilicate glass-ceramic materialhas a coarse crystalline phase, there is a limitation in realizing highlight transmittance or opalescence similar to those of a natural tooth.

In particular, in order to machine the existing lithium disilicateglass-ceramic material, lithium metasilicate glass-ceramics havingexcellent machinability are primarily prepared, and then, lithiumdisilicate is prepared through a secondary crystallization heattreatment to improve strength. In this case, a crystalline phase has asize of 3 μm or more. In this state, machinability is considerablylowered and only high strength is obtained.

SUMMARY OF THE INVENTION

An aspect of the present invention is directed to propose a method forpreparing a glass-ceramics containing a lithium disilicate crystallinephase, a silicate crystalline phase, and a silica crystalline phase,which have excellent machinability, by adjusting a (nanoscale)crystalline size through a change in a temperature of a first heattreatment.

Another aspect of the present invention is directed to propose a methodfor preparing a glass-ceramics, which is capable of adjustingtranslucency by adjusting crystalline sizes of lithium disilicate,silicate, and silica, which have a nano crystalline phase.

According to an embodiment of the present invention, a glass compositionincludes: 60 to 83 wt % SiO₂; 10 to 15 wt % Li₂O; 2 to 6 wt % P₂O₅working as a nuclei formation agent; 1 to 5 wt % Al₂O₃ for increasing aglass transition temperature and a softening point and enhancingchemical durability of a glass; 0.1 to 3 wt % SrO for increasing thesoftening point of the glass; 0.1 to 2 wt % ZnO; 1 to 5 wt % colorants;and 2.5 to 6 wt % alkali and alkaline-earth mixture (Na₂O+K₂O) forincreasing a thermal expansion coefficient of the glass.

According to an embodiment of the present invention, a method forpreparing a glass-ceramics containing a silica crystalline phaseincludes performing a first heat treatment on a glass composition at atemperature of 400 to 850° C., so that a lithium disilicate crystallinephase and a silica crystalline phase each having a size of 5 to 2,000 nmare formed through the first heat treatment.

According to an embodiment of the present invention, the method furtherincludes, after the first heat treatment, performing a second heattreatment at a temperature of 780 to 880° C., so that translucency isadjusted by a temperature of the second heat treatment.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a scanning electron microscope (SEM) image of a microstructurewhen a first heat treatment was performed on a starting raw material.

FIG. 2 is a graph showing an X-ray diffraction analysis of a crystallinephase when a first heat treatment was performed on a starting rawmaterial.

FIG. 3 is a graph showing measurement results of a crystalline size andmachining resistance (machinability of cutting force) of lithiumdisilicate according to a temperature of a first heat treatment.

FIG. 4 is a graph showing translucency spectrum result data according toa temperature of a second heat treatment.

FIG. 5 is a graph showing measurement results of a crystalline size andtransmittance of lithium disilicate according to a temperature of asecond heat treatment.

DETAILED DESCRIPTION OF EMBODIMENTS

The present invention relates to a glass material, whose crystallinesize is adjustable through a temperature of a heat treatment, and amethod for preparing a glass-ceramics for a dental material. The dentalmaterial is applicable only when it has translucent aesthetics andmachinability. The present invention is directed to obtain aestheticsand machinability required by the dental material by developing a glasscomposition, whose crystalline size and crystal distribution areadjustable according to a temperature of a heat treatment.

A high-strength glass-ceramics for a tooth according to the presentinvention includes a silica crystalline phase, a lithium disilicatecrystal, and hyaline. Since the high-strength glass-ceramics exhibits avery similar color to that of a natural tooth as a whole, thehigh-strength glass-ceramics is highly aesthetic and is suitable for useas a dental material.

The aesthetics, particularly, light transmittance is largely affected bythe degree of light scattering caused by a difference in refractiveindex between different crystallines in dense bulk. The SiO₂ cluster hasa refractive index of 1.48. As a content of the SiO₂ cluster increases,an interface between the SiO₂ cluster and mother glass or a lithiumdisilicate crystalline phase increases. Accordingly, transmittancedecreases due to high scattering of light. Therefore, in order to obtainlight-transmitting properties usable for the dental material, aprosthetic material having various light-transmitting properties may beprepared by forming an appropriate amount of only a SiO₂ clustercrystalline phase within a glass.

In the case of an existing lithium disilicate glass-ceramics, aprosthesis has been manufactured by primarily forming a lithiummetasilicate glass-ceramics having low strength of 220 MPa or less,machining the lithium metasilicate glass-ceramics, and increasingstrength to 350 MP through a secondary heat treatment. However, sincethese translucencies have already been determined according to acomposition or the like in a block state, as many products andquantities as the number of required translucencies are required, andthe number of implementable translucencies is limited.

The present invention proposes a material that is machinable in a stateof lithium disilicate rather than an existing lithium metasilicatecrystalline phase by forming a lithium disilicate crystalline phase anda silica crystalline phase having a nanosize. At the same time,machinability and transmittance may be adjusted according to acrystallization temperature. Therefore, it is possible to manufacture aproduct having desired transmittances at different temperatures in oneproduct and also manufacture a product having various translucencies inone product. Due to a crystal grown after a second heat treatment,mechanical properties are increased, and in particular, biaxial flexurestrength of 490 MPa or more is exhibited.

This may meet needs of customers who want various translucencies, andphysical properties also are improved compared to an existing product.

According to the present invention, a glass containing a silicacrystalline phase includes 60 to 83 wt % SiO₂, 10 to 15 wt % Li₂O, 2 to6 wt % P₂O₅ working as a nuclei formation agent, 1 to 5 wt % Al₂O₃ forincreasing a glass transition temperature and a softening point andenhancing chemical durability of the glass, 0.1 to 3 wt % SrO forincreasing the softening point of the glass, 0.1 to 2 wt % ZnO, 1 to 5wt % colorants, and 2.5 to 6 wt % alkali and alkaline-earth mixture(Na₂O+K₂O) for increasing a thermal expansion coefficient of the glass.

The dental high-strength glass-ceramics according to the exemplaryembodiment of the present invention may further include 1 to 5 wt %colorant as described above in order to provide the same or similarcolor as or to the teeth. The colorant is to provide the same or similarcolor and fluorescence as or to the teeth and may use red iron oxide(Fe₂O₃), yellow ceria (CeO₂), orange vanadium pentoxide (V₂O₅), blackvanadium trioxide V₂O₃, Er₂O₃, Tb₂O₃, Pr₂O₃, TaO₂, MnO₂, or a mixturethereof. For example, red iron oxide (Fe₂O₃), ceria (CeO₂), or vanadiumpentoxide (V₂O₅) is added together with starting materials to be meltedto have a light yellow which is similar to the teeth's color. Titaniumoxide (TiO₂) has white to provide a very similar color to the teeth'scolor.

The aforementioned starting materials are measured and mixed. In thiscase, Li₂CO₃ instead of Li₂O may be added and carbon dioxide (CO₂) as acarbon (C) component of Li₂CO₃ is discharged and removed as gas in amelting process of the glass. Further, in alkali oxide, K₂CO₃ and Na₂CO₃instead of K₂O and Na₂O may be added, respectively, and carbon dioxide(CO₂) as carbon (C) components of K₂CO₃ and Na₂CO₃ is discharged andremoved as gas in a melting process of the glass.

The mixing process uses a dry mixing process, and a ball milling processand the like may be used as the dry mixing process. When describing theball milling process in detail, the starting materials are put in a ballmilling machine and mechanically grinded and uniformly mixed by rotatingthe ball milling machine at a predetermined speed. The balls used in theball milling machine may use balls made of ceramic materials such aszirconia or alumina, and the sizes of the balls may be the same as eachother or has at least two sizes. The size of the ball, milling time, rpmof the ball milling machine, and the like are controlled by consideringa desired size of the particle. In an example, taking into account aparticle size, a size of a ball may be set to a range of 1 to 30 mm, anda rotational speed of a ball milling machine may be set to a range of 50to 500 rpm. Taking into account a targeted particle size or the like, itis desirable that ball milling is performed for 1 to 48 hours. Astarting raw material is pulverized into fine particles through the ballmilling, and the fine particles have a uniform particle size and arealso uniformly mixed.

The mixed starting material is put in a melting furnace and melted byheating the melting furnace with the starting material. Herein, themelting means that the starting materials are changed into a materialstate having viscosity in a liquid state other than a solid state. It ispreferred that the melting furnace is made of a material having a highmelting point, a large strength, and a low contact angle in order tosuppress a molten material from being attached. To this end, it ispreferred that the melting furnace is a melting furnace made of amaterial such as platinum (Pt), diamond-like-carbon (DLC), and chamotteor coated on the surface with a material such as platinum (Pt) ordiamond-like-carbon (DLC).

The melting is performed for 1 to 12 hours at atmospheric pressure. Whenthe melting temperature is less than 1,400° C., the starting materialsmay not be melted. When the melting temperature is more than 2,000° C.,the starting materials are not economic due to excessive energyconsumption, and thus, it is preferred that the starting materials aremelted in the aforementioned range. Further, when the melting time istoo short, the starting materials may not be sufficiently melted, andwhen the melting time is very large, the starting materials are noteconomic due to excessive energy consumption. It is preferred that theheating rate of the melting furnace is 5 to 50° C./min. When the heatingrate of the melting furnace is very slow, a lot of time is taken andthus, productivity is deteriorated, and when the heating rate of themelting furnace is very fast, the volatile amount of the startingmaterials is increased, and thus, the property of the glass-ceramics maybe bad. As a result, it is preferred that the temperature of the meltingfurnace is increased at the heating rate in the aforementioned range. Itis preferred that the melting is performed at an oxygen atmosphere suchas air.

In order to obtain the dental glass-ceramics having desired shape andsize, the molten material is poured in a predetermined mold. It ispreferred that the mold is made of a material having a high meltingpoint, a large strength, and a low contact angle for suppressing theglass molten material from being attached. To this end, the mold is madeof a material such as graphite and carbon, and it is preferred that themolten material is preheated at 200 to 300° C. and poured in the mold inorder to prevent thermal shock.

When a molten material contained in a mold is cooled to a temperature of60 to 100° C., the cooled molten material is transferred to acrystallization heat treatment furnace and a glass-ceramics is preparedby performing nuclei formation and crystal growth on the glass. This isbecause, in a method capable of variously adjusting machinability andtranslucency of the glass through first and second heat treatments asproposed in the present invention, a crystalline size in theglass-ceramics is adjustable according to a temperature. A crystallinephase formed after the first heat treatment includes a lithiumdisilicate crystalline phase and a silica crystalline phase each havinga crystalline size of 5 to 2,000 nm at a temperature of 400 to 850° C.Machinability of cutting force may be obtained when a crystalline phase(lithium disilicate or silica) has a crystalline size of 30 to 500 nmcorresponding to a temperature of 480 to 800° C.

When a final prosthesis is completed through the second heat treatment,a clinical treatment needs products having various translucencies. Atthis time, transmittance generally corresponds to 20 to 55% (at awavelength of 550 nm). When the second heat treatment was performed at atemperature of 780 to 900° C., transmittance was 55 to 18% (at awavelength of 550 nm). Transmittance was reduced at a temperature of880° C. or more, and it was analyzed that transmittance applicable to aclinical treatment was obtained at a temperature of 780 to 880° C. Atthis time, a size of a crystalline phase (lithium disilicate crystallinephase or silica crystalline phase) corresponds to 0.3 to 5.5 μm andtransmittance was 27 to 55% (at a wavelength of 550 nm).

Therefore, the present invention proposes a method for preparing glass,capable of adjusting machinability and translucency, which are actuallyusable for a clinical treatment, through the first and second heattreatments, and a heat treatment condition.

FIG. 1 is a scanning electron microscope (SEM) image of a microstructurewhen a first heat treatment was performed on a starting raw material,and in particular, the first heat treatment was performed at atemperature 750° C. Referring to FIG. 1, it can be seen that, when thefirst heat treatment was performed at a temperature of 750° C., thereexisted a globular SiO₂ crystalline phase having a similar size toacicular lithium disilicate having a size of about 100 to about 2,000nm. That is, it can be seen that, when the first heat treatment wasperformed on a general starting raw material, there existed no globularSiO₂ crystalline phase, but when the first heat treatment was performedon the starting raw material proposed in the present invention, thereexisted the globular SiO₂ crystalline phase.

FIG. 2 is a graph showing an X-ray diffraction analysis of a crystallinephase when a first heat treatment was performed on a starting rawmaterial, and in particular, the first heat treatment was performed at atemperature of 750° C. Referring to FIG. 2, it can be seen from theX-ray diffraction analysis that crystals shown in FIG. 1 were a lithiumdisilicate crystal and a SiO₂ crystal.

FIG. 3 is a graph showing measurement results of a crystalline size andmachining resistance (machinability of cutting force) of lithiumdisilicate according to a temperature of a first heat treatment.Referring to FIG. 3, a black graph indicates a crystalline size oflithium disilicate, and a red graph indicates a cutting force. Accordingto the graphs, it can be confirmed that, as a crystalline sizeincreases, a cutting force increases. When the cutting force increases,a high load is applied to a cutting bur, thus deterioratingmachinability. Therefore, according to the present invention, it can beseen that a crystalline phase having a size of 30 to 500 nmcorresponding to a temperature of 480 to 800° C. has excellentmachinability.

FIG. 4 is a graph showing translucency spectrum result data according toa temperature of a second heat treatment.

A lithium disilicate crystalline phase and the silica crystalline phaseeach have high translucency at a temperature of 780 to 820° C., mediumtranslucency at a temperature of 821 to 840° C., low translucency at atemperature of 841 to 860° C., and medium opacity at a temperature of861 to 880° C., and a retention time is 1 minute to 2 hours. Referringto FIG. 4, as a temperature increases, translucency decreases from hightranslucency to medium opacity.

FIG. 5 is a graph showing measurement results of a crystalline size andtransmittance of lithium disilicate according to a temperature of asecond heat treatment. The present invention is characterized in thattransmittance is adjustable according to a temperature of a heattreatment with respect to a glass-ceramics. In the case of FIG. 5, ablack graph indicates a crystalline size of lithium disilicate, and ared graph indicates transmittance. It can be seen from FIG. 5 that asthe temperature of the second heat treatment increases, the crystallinesize increases, and as the crystalline size increases, transmittancedecreases. As the crystalline size increases, a ratio of absorption andreflection of light further increase rather than transmission of light,thus reducing the transmittance. Therefore, it can be confirmed that itis possible to prepare a glass-ceramics exhibiting varioustransmittances according to a change in the temperature of the secondheat treatment even in the glass-ceramics having one composition.

Machinability and translucency of glass proposed in the presentinvention may be variously adjusted through a first heat treatment or asecond heat treatment. Generally, a crystalline size in a glass-ceramicsmay be adjusted according to a temperature. According to the presentinvention, a lithium disilicate crystalline phase and a silicacrystalline phase are formed through a first heat treatment. Inparticular, a crystalline phase formed through the first heat treatmentis formed at a temperature of 480 to 800° C. so as to increasemachinability of cutting force. At this time, the formed crystallinephase has a size of 30 to 500 nm.

In addition, when a final prosthesis is completed, a clinical treatmentneeds products having various translucencies. The present inventionproposes a product having transmittance of 27 to 55% (at a wavelength of550 nm) through the second heat treatment.

As described above, the present invention proposes a method forpreparing a glass-ceramics, capable of adjusting machinability andtranslucency, which are actually usable for a clinical treatment,through the first and second heat treatment conditions.

While the present invention has been described with reference to anembodiment, it will be apparent to those skilled in the art that variouschanges and modifications may be made without departing from the spiritand scope of the inventive concept.

What is claimed is:
 1. A glass composition for dental materialscomprising: 60 to 83 wt % SiO₂; 10 to 15 wt % Li₂O; 2 to 6 wt % P₂O₅working as a nuclei formation agent; 1 to 5 wt % Al₂O₃ for increasing aglass transition temperature and a softening point and enhancingchemical durability of glass; 0.1 to 3 wt % SrO for increasing thesoftening point of the glass; 0.1 to 2 wt % ZnO; 1 to 5 wt % colorants;and 2.5 to 6 wt % mixture of Na₂O and K₂O for increasing a thermalexpansion coefficient of the glass, wherein the glass composition issubjected to a first heat treatment at a temperature of 480 to 800° C.to form a lithium disilicate crystalline phase and a silica crystallinephase each having a size of 30 to 500 nm.
 2. A method for preparing aglass-ceramics containing a silica crystalline phase, the methodcomprising: performing a first heat treatment on the glass compositionof claim 1 at a temperature of 480 to 800° C., so that a lithiumdisilicate crystalline phase and a silica crystalline phase each havinga size of 30 to 500 nm are formed through the first heat treatment. 3.The method of claim 2, further comprising, after the first heattreatment, performing a second heat treatment at a temperature of 780 to880° C., so that translucency of the glass ceramics is adjusted based onthe temperature of the second heat treatment.
 4. The method of claim 3,wherein the lithium disilicate crystalline phase and the silicacrystalline phase each have a size of 0.3 to 5.5 μm after the secondheat treatment.